US6558486B1 - Method of producing cold rolled steel strip - Google Patents

Method of producing cold rolled steel strip Download PDF

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Publication number
US6558486B1
US6558486B1 US09/889,081 US88908101A US6558486B1 US 6558486 B1 US6558486 B1 US 6558486B1 US 88908101 A US88908101 A US 88908101A US 6558486 B1 US6558486 B1 US 6558486B1
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strip
range
thickness
cold
produces
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US09/889,081
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Lazar Strezov
Kannappar Mukunthan
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Nucor Corp
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Castrip LLC
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Priority to US10/329,869 priority Critical patent/US6841010B2/en
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • C21D8/0215—Rapid solidification; Thin strip casting
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C21D1/30—Stress-relieving
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium

Definitions

  • the invention provides a method of producing plain carbon steel strip which has an excellent balance of ultimate tensile strength and elongation to break making it particularly suitable for the production of structural steel products.
  • Strip produced in accordance with the invention may for example be used as a feed material that is hot dip coated with zinc or aluminium/zinc alloys to produce roof decking, guttering and other structural steel products.
  • strip as used in the specification is to be understood to mean a product of 5 mm thickness or less.
  • the molten metal may be poured from a ladle into a smaller vessel from which it flows through a metal delivery nozzle located above the nip so as to direct it into the nip between the rolls, so forming a casting pool of molten metal supported on the casting surfaces of the rolls immediately above the nip and extending along the length of the nip.
  • This casting pool is usually confined between side plates or dams held in sliding engagement with end surfaces of the rolls so as to dam the two ends of the casting pool against outflow, although alternative means such as electromagnetic barriers have also been proposed.
  • the casting of steel strip in twin roll casters of this kind is for example described in U.S. Pat. Nos. 5,184,668, 5,277,243 and 5,934,359.
  • a silicon/manganese killed steel will generally have a manganese content of not less than 0.20% (typically about 0.6%) by weight and a silicon content of not less than 0.10% (typically about 0.3%) by weight.
  • G 550 steel strip is produced by casting plain carbon steel slabs, hot rolling the slabs to form strip and thereafter coiling the strip, uncoiling and thereafter cold rolling the strip to a final product size of 0.25-2 mm, and heat treating the cold rolled strip to produce the final product.
  • G 550 steel strip has a guaranteed minimum ultimate tensile strength of 550 MPa and in a number of instances has ultimate tensile strengths above 700 MPa.
  • G 550 steel strip (Zincalume G 550 coated steel) that is produced from plain carbon steel and is used for roof decking has an ultimate tensile strength of 680-780 MPa (based on a test sample of 0.42 mm thickness and an original gauge length of 80 mm).
  • this G 550 steel strip only has an elongation-to-break of 1-6%.
  • the present invention enables production of a plain carbon steel strip of comparable tensile strength but an even better elongation-to-break.
  • a method of producing steel strip comprising continuously casting plain carbon steel into a strip of no more than 5 mm thickness
  • the cold rolling produces a cold reduction in a range which is sufficient to increase the tensile strength of the strip to at least 680 MPa but such that the total elongation to break of the strip after said annealing is in the range 8% to 12%.
  • the tensile strength of the strip may be at least 700 MPa.
  • the continuous strip casting step may be carried out by means of a twin roll strip caster.
  • plain carbon steel is understood to mean steel of the following composition, in weight percent:
  • Si 0.5 or less
  • Mn 1.0 or less
  • residual/incidental impurities covers levels of elements, such as copper, tin, zinc, nickel, chromium, and molybdenum, that may be present in relatively small amounts, not as a consequence of specific additions of these elements but as a consequence of standard steel making.
  • the elements may be present as a result of using scrap steel to produce plain carbon steel.
  • (b) amounts of elements, such as the elements listed in the preceding paragraph that are specifically added to the steel for the purpose of strengthening the steel.
  • the plain carbon steel may be silicon/maganese killed and may have the following composition by weight:
  • a typical composition is as follows:
  • the cold rolling may produce a cold reduction of the strip thickness in the range 40% to 80%.
  • the annealing may produce the stress relieved microstructure with no more than 10% recrystallisation and an elongation-to-break of at least 10%.
  • the annealing temperature may be at least 450° C. and may be in the range 500° C. to 600° C.
  • the continuously cast strip may be in-line hot rolled to reduce the thickness of the strip prior to coiling. It is desirable that the hot rolling produce a thickness reduction of no more than 40%.
  • the subsequent cold rolling produces a cold reduction of the strip in the range 40% to 60%.
  • the invention further provides a plain carbon steel strip having an ultimate tensile strength of at least 700 MPa and an elongation to break in the range of 8% to 12%.
  • FIG. 1 illustrates a strip casting installation incorporating an in-line hot rolling mill and coiler
  • FIG. 2 illustrates details of the twin roll strip caster
  • FIG. 3 illustrates an uncoiling and cold rolling installation
  • FIGS. 4 to 13 provide test data obtained from a series of experiments in which plain carbon steel strips cast in a twin roll caster were subjected to cold roll reduction, and in some cases to initial in-line hot rolling, and were subsequently annealed at various annealing temperatures.
  • FIGS. 1 and 3 illustrate successive parts of production line whereby steel strip can be produced in accordance with the present invention.
  • FIGS. 1 and 2 illustrate a twin roll caster denoted generally as 11 which produces a cast steel strip 12 that passes in a transit path 10 across a guide table 13 to a pinch roll stand 14 comprising pinch rolls 14 A.
  • the strip passes into a hot rolling mill 16 comprising a pair of reduction rolls 16 A and backing rolls 16 B in which it is hot rolled to reduce its thickness.
  • the rolled strip passes onto a run-out table 17 on which it may be force cooled by water jets 18 and through a pinch roll stand 20 comprising a pair of pinch rolls 20 A, and thence to a coiler 19 .
  • twin roll caster 11 comprises a main machine frame 21 which supports a pair of parallel casting rolls 22 having casting surfaces 22 A.
  • Molten metal is supplied during a casting operation from a ladle (not shown) to a tundish 23 , through a refractory shroud 24 to a distributor 25 and thence through a metal delivery nozzle 26 into the nip 27 between the casting rolls 22 .
  • Molten metal thus delivered to the nip 27 forms a pool 30 above the nip and this pool is confined at the ends of the rolls by a pair of side closure dams or plates 28 which are applied to the ends of the rolls by a pair of thrusters (not shown) comprising hydraulic cylinder units connected to the side plate holders.
  • the upper surface of pool 30 (generally referred to as the “meniscus” level) may rise above the lower end of the delivery nozzle so that the lower end of the delivery nozzle is immersed within this pool.
  • Casting rolls 22 are water cooled so that shells solidify on the moving roll surfaces and are brought together at the nip 27 between them to produce the solidified strip 12 which is delivered downwardly from the nip between the rolls.
  • twin roll caster may be of the kind which is illustrated and described in some detail in U.S. Pat. Nos. 5,184,668 and 5,277,243 or U.S. Pat. No. 5,488,988 and reference may be made to those patents for appropriate constructional details which form no part of the present invention.
  • FIG. 3 illustrates an uncoiler 31 by which a coil produced on the apparatus may be uncoiled.
  • the uncoiled strip 12 is passed through a pinch roll stand 32 to a cold rolling mill 33 comprising reduction rolls 33 A and backing rolls 33 B and thence through an annealing enclosure 34 .
  • Hot strip mill products undergo large reduction which breaks up the original slab microstructure through enhanced recrystallisation kinetics resulting in significant refinement of austenite grains (approximately 20 microns), which upon transformation produce a fine equiaxed ferrite grain structure (approximately 10 microns—this is a completely polygonal microstructure).
  • the austenite grain size (typically 150-250 microns in width and 500 microns in length) in cast strip is entirely governed by the casting process and such coarse austenite grains when transformed result in a mixed microstructure consisting of coarse polygonal ferrite grains (typically 10-50/50-250 microns width/length and 30-60% in volume fraction for standard cooling/coiling conditions) and relatively fine Widmanstatten/acicular ferrite.
  • Scope for grain refinement is, limited, primarily because the coarse austenite grains are inherently resistant to recrystallisation and also due to the fact that only a single hot rolling pass is available under normal strip casting plant layout. However, considerable amount of grain refinement is observed when the amount of hot reduction is greater than 30%, resulting in polygonal ferrite content of greater than 80% with grains in the range of 10-50 microns.
  • the run-out-table cooling/coiling conditions determine the initial as-cast microstructure.
  • the microstructure described previously is obtained under typical operating conditions; cooling rate of 10-20° C./s and coiling temperature of 600-700° C. These conditions usually result in total elongation values of 20-30% and such initial properties are ideal to produce strip with the necessary balance of tensile strength and elongation.
  • the initial elongation can be as low as 15% and this will reduce the cold rolling range to produce the required elongation value in the final product.
  • a first series of experiments was carried out on samples of 2.17 mm thickness as-cast plain carbon steel strip cast at a casting speed of 34 m/min.
  • the steel was a silicon/manganese killed steel with a carbon content of 0.06% (by weight), a manganese content of 0.6%, a silicon content of 0.3% and a sulphur content of 0.01%.
  • the samples were divided into groups and were cold rolled to produce thickness reductions of 20%, 40%, 60%, 80% and 90%.
  • a set of the samples from each group was then heat treated in a fluidised bed furnace for 60 seconds at 500° C.
  • a further set of the samples from each group was heat treated for 60 seconds at 550° C. in the furnace.
  • a third set of the samples from each group was heat treated for 60 seconds at 600° C. in the furnace.
  • the cold rolled and annealed sets of samples and a fourth set of the cold rolled samples were then tested in a tensile testing machine to determine the ultimate tensile strengths and elongations-to-break of the samples.
  • the tensile tests were carried out according to Australian Standard 1391 (AS1391).
  • the test samples had a gauge length of 12 mm and a parallel length of 22 mm.
  • FIG. 4 is a graph of ultimate tensile strength and elongation-to-break versus cold reduction for the samples.
  • FIG. 5 is a graph of ultimate tensile strength and elongation-to-break versus cold reduction for the samples.
  • FIGS. 4 and 5 demonstrate a significant drop in elongation occurring at 80% cold reduction for strip which is cold rolled in the as cast condition and at 60% cold reduction for the hot rolled strip. This indicates that when the strip is initially hot rolled, this will reduce the maximum allowable cold reduction with the minimum elongation-to-break of 8% is to be maintained.
  • FIGS. 6 and 7 provide the same experimental data as previously presented in FIGS. 4 and 5 with some additional data obtained with 50 mm gauge samples. This shows that ultimate tensile strength values of at least 680 MPA and elongation-to-break of at least 10% are also measured for 50 mm gauge samples.
  • FIGS. 8 and 9 show the increased recovery effects on total elongation with increased annealing temperatures in the range from 500° C. to 600° C.
  • FIG. 8 is derived from data initially presented in FIG. 4 and plots the ratio of increased elongation on annealing for differing percentages of cold reduction and that annealing temperatures of 500° C., 550° C. and 600° C.
  • FIG. 9 plots equivalent values obtained from the initially hot rolled strips as initially plotted in FIG. 5 .
  • FIGS. 10 and 11 plot data obtained from a series of experiments carried out with plain carbon steel strip samples produced at different casting speeds resulting in different initial microstructure and different initial elongation properties in the as cast strip.
  • the steel was a silicon/manganese killed steel of essentially the same composition as for the previous experiments which produced the data of FIGS. 4 to 9 .
  • FIG. 10 plots tensile strength values obtained on 50 mm gauge samples of 2.07 mm strip which was cast at a casting speed of 37 m/min and had an initial elongation-to-break of around almost 30% in the as cast condition, the strip then being subjected to cold reductions of 20%, 40%, 60%, 80% and 90% and subsequent annealing at temperatures of 500° C., 550° C. and 600° C.
  • FIG. 11 plots comparable results obtained from 50 mm gauge samples of a cast strip cast at a casting speed of 100 m/min and having an initial thickness of 1.30 mm and an initial total elongation-to-break of around 20% in the as cast condition.
  • the data plotted in FIGS. 10 and 11 shows that with a high elongation starting material it is possible to achieve tensile strengths of 700 MPa and elongation-to-break values in the range 8% to 12% with up to 80% cold reduction.
  • a low elongation starting material about 20% elongation
  • FIGS. 12 and 13 provide data obtained from experiments on strip produced by twin roll casting from a silicon/manganese killed plain carbon steel with high residuals, specifically a steel having the maximum residuals of 0.2 Cr, 0.2 Ni, 0.2 Mo, 0.2 Sn and 0.5 Cu.
  • the strip was cast at a casting speed of 55 m/min and was in-line hot rolled to a 25% reduction at 1050° C.
  • Various samples from the hot rolled coil were then cold rolled to 20%, 40%, 60% and 80% reduction and annealed at various annealing temperatures from 500° C. to 800° C.
  • FIG. 12 shows the evolution of measured tensile strength of the samples during annealing
  • FIG. 13 shows the evolution of total elongation during annealing.
  • This data shows tensile strength values of 700 to 850 MPa and elongation values in the range 8% to 12% (on a 50 mm gauge) for a range of cold rolling reductions of 20% to 60% at annealing temperatures of 600° C. to 660° C. Residuals severely retarded the onset of recrystallisation thereby allowing high annealing temperatures of 600° C. to 660° C. to be employed without any observable recrystallisation during annealing. These results show residuals can be extremely beneficial and can produce an extended range of properties. Moreover, the inclusion of high residuals can offset reduced work hardening with lower manganese and silicon contents and may even permit the required balance of tensile strength and elongation values to be achieved with aluminium killed plain carbon steel.

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  • Child & Adolescent Psychology (AREA)
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US09/889,081 1999-01-12 2000-01-11 Method of producing cold rolled steel strip Expired - Lifetime US6558486B1 (en)

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US20040144518A1 (en) * 2003-01-24 2004-07-29 Blejde Walter N. Casting steel strip with low surface roughness and low porosity
US20050145304A1 (en) * 2003-01-24 2005-07-07 Blejde Walter N. Casting steel strip
US20060144553A1 (en) * 2001-09-14 2006-07-06 Nucor Corporation Steel product with a high austenite grain coarsening temperature, and method for making the same
US20060196630A1 (en) * 2001-09-14 2006-09-07 Nucor Corporation Casting steel strip
US20070079950A1 (en) * 2001-09-14 2007-04-12 Nucor Corporation Thin cast strip with controlled manganese and low oxygen levels and method for making same
US20070090161A1 (en) * 2003-10-10 2007-04-26 Nucor Corporation Casting steel strip
US20080219879A1 (en) * 2005-10-20 2008-09-11 Nucor Corporation thin cast strip product with microalloy additions, and method for making the same
US20100186856A1 (en) * 2005-10-20 2010-07-29 Nucor Corporation High strength thin cast strip product and method for making the same
US9999918B2 (en) 2005-10-20 2018-06-19 Nucor Corporation Thin cast strip product with microalloy additions, and method for making the same
US11193188B2 (en) 2009-02-20 2021-12-07 Nucor Corporation Nitriding of niobium steel and product made thereby

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AUPR047900A0 (en) * 2000-09-29 2000-10-26 Bhp Steel (Jla) Pty Limited A method of producing steel
AU9150501A (en) * 2000-09-29 2002-04-08 Ishikawajima Harima Heavy Ind Production of thin steel strip
US7591917B2 (en) 2000-10-02 2009-09-22 Nucor Corporation Method of producing steel strip
CN102943164B (zh) * 2012-11-14 2014-08-20 河北钢铁股份有限公司 一种高屈强比spcc薄钢板冷轧及连续退火工艺方法
RU2583536C1 (ru) * 2014-10-21 2016-05-10 Публичное акционерное общество "Северсталь" (ПАО "Северсталь") Способ производства горячекатаных листов для строительных стальных конструкций (варианты)
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CN105256224A (zh) * 2015-11-11 2016-01-20 攀钢集团攀枝花钢铁研究院有限公司 油汀用冷轧微碳钢带及其制备方法
CN113751679B (zh) * 2021-09-09 2022-10-28 中南大学 一种无钴马氏体时效钢冷轧薄带的制造方法

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USRE31306E (en) * 1975-02-28 1983-07-12 Armco Inc. Cold rolled, ductile, high strength steel strip and sheet and method therefor
DE3105891A1 (de) 1981-02-18 1982-09-02 Rudolf Dipl.-Ing.Dr. 4150 Krefeld Oppenheim Verwendung eines schweissbaren nichtrostenden stahles fuer kettenglieder
EP0073092A1 (en) 1981-08-13 1983-03-02 Kawasaki Steel Corporation Method of manufacturing T-3 grade low temper blackplates

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EP1157138B1 (en) 2009-05-27
MXPA01007029A (es) 2004-09-06
ID29959A (id) 2001-10-25
NZ512783A (en) 2002-09-27
ZA200105726B (en) 2002-02-25
EP1157138A1 (en) 2001-11-28
CN1143899C (zh) 2004-03-31
EP1157138B9 (en) 2009-10-21
DK1157138T3 (da) 2009-09-21
US20030106621A1 (en) 2003-06-12
JP4834223B2 (ja) 2011-12-14
BR0007480A (pt) 2001-10-23
MY126765A (en) 2006-10-31
CA2359818A1 (en) 2000-07-20
BR0007480B1 (pt) 2011-03-22
CN1340106A (zh) 2002-03-13
JP2002534611A (ja) 2002-10-15
KR100665164B1 (ko) 2007-01-04
ATE432369T1 (de) 2009-06-15
WO2000042228A1 (en) 2000-07-20
AUPP811399A0 (en) 1999-02-04
US6841010B2 (en) 2005-01-11
TW469180B (en) 2001-12-21
KR20010093258A (ko) 2001-10-27
EP1157138A4 (en) 2005-08-31
DE60042266D1 (de) 2009-07-09

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